CN109778032A - A kind of preparation method of aluminum alloy plate materials - Google Patents
A kind of preparation method of aluminum alloy plate materials Download PDFInfo
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- CN109778032A CN109778032A CN201811568759.4A CN201811568759A CN109778032A CN 109778032 A CN109778032 A CN 109778032A CN 201811568759 A CN201811568759 A CN 201811568759A CN 109778032 A CN109778032 A CN 109778032A
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Abstract
A kind of preparation method of aluminum alloy plate materials of the present invention, the following compositions of aluminium alloy meter containing weight percent: Zn 8.0~12.0%, Cu 1.0~6.5%, Li 1.4~1.80%, Mg 0.2~3.5%, Mn 0.10~1.30%, and Zr 0.02~0.25%, Sc 0.05~0.35%, Ag 0.2~0.8%, any 1~4 kind in Er 0.10~0.25%, Si≤0.15%, Fe≤0.15%, Ti≤0.10%, other impurity are single≤and 0.05%, total amount≤0.15%, surplus Al.The method includes: rolling deformation after being during the rolling process quickly cooled down plate, the plate is precipitated quickly through " Wei Shi body " in the hot rolling, and deformation and energy storage is introduced by middle temperature rolling, make plate that certain recrystallization occur with coarse remaining second phase core in subsequent solution treatment, eliminate the original grain boundary that ingot casting " heredity " is directed at, the tissue signature for obtaining crystal boundary " pure ", to improve the comprehensive performance of aluminium alloy.Method provided by the invention is suitable for the aluminium alloy thick plate of Aeronautics and Astronautics, weapons field.
Description
Technical field
The present invention relates to a kind of preparation methods of plate, and in particular to a kind of preparation method of aluminum alloy plate materials.
Background technique
With the continuous development of highly reliable, the high loss of weight demand of aerospace field, by the content for increasing alloy element
And corresponding preparation method obtains the trend that the aluminium alloy of high combination property has become development.In order to realize this mesh
Mark is also taken both at home and abroad while carrying out a large amount of heat treatments (T77 T78 etc.) research and improves alloy element and contain
It measures to improve the research of alloy comprehensive performance.However, with the raising of alloying element content, while alloy strength is promoted,
As cast condition eutectic structure is transformed into remaining second phase of a large amount of large scale, while transgranular precipitation in annealing process after hot rolling when homogenizing
Largely " Wei Shi body " tissue, these tissues have strong " heredity " effect, are difficult in subsequent solid solution, ag(e)ing process completely
It eliminates, so as to cause the deterioration of the comprehensive performances such as the plasticity, fracture toughness, corrosive nature of alloy, is unable to satisfy use demand, directly
Affect the application of alloy.
There are the large scale remnants second for being largely difficult to eliminate in crystal boundary for high alloy content aluminum alloy plate materials in the present invention
The problem of mutually and present on crystal boundary, sub boundary large-size flaky " Wei Shi body " tissue is to influence alloy comprehensive performance, leads to
The methods of rapid cooling+temperature-controlled rolling in the operation of rolling is crossed, in conjunction with subsequent solution treatment, on the one hand inhibits large scale
The precipitation of " Wei Shi body " is on the other hand the recrystallization of core, the remnants that will be distributed in crystal boundary/sub boundary by remaining second phase
Second phase transition is transgranular distribution, to increase substantially fracture toughness, the modeling of alloy while not reducing alloy strength
Property, corrosion resisting property, obtain have excellent comprehensive performance product.
Summary of the invention
The purpose of the present invention is:
A kind of preparation method of aluminum alloy plate materials is proposed, in this way, the feelings that sheet alloy can be made not reduce in intensity
Under condition, the comprehensive performances such as plasticity, fracture toughness, corrosive nature, fatigue behaviour obtain larger promotion.
The technical scheme is that
A kind of preparation method of aluminum alloy plate materials, it is improved in that by alloy hot rolling, rapid cooling, it is secondary rolling,
Solution hardening, pre-stretching and artificial aging processing；By weight percentage, which contains: Zn 8.0~12.0%, Cu 1.0~
6.5%, Li1.4~1.80%, Mg 0.2~3.5%, Mn 0.10~1.30% and Zr 0.02~0.25%, Sc 0.05
Any 1~4 kind in~0.35%, Ag 0.2~0.8%, Er 0.10~0.25%, Si≤0.15%, Fe≤0.15%, Ti
≤ 0.10%, other impurity are single≤and 0.05%, total amount≤0.15%, surplus Al.
Preferred a kind of preparation method of aluminum alloy plate materials, it is improved in that the alloying component are as follows: Zn
8.0%, Cu 3.5%, Li 1.70%, Mg 0.38%, Mn 0.44% and Zr 0.10%, Sc 0.10%, Ag
Any 1~4 kind in 0.35%, Er 0.10, Si 0.06%, Fe 0.08%, Ti 0.06%, other impurity are single≤
0.05%, total amount≤0.15%, surplus Al.
A kind of preferred preparation method of aluminum alloy plate materials, thes improvement is that:
3.1 hot rolling treatments include: the blank material that stove heating is heated in hot rolling at 380 DEG C~560 DEG C, until predetermined deformation amount
75%~90%；
The 3.2 rapid cooling processing include: to be blown with lotion, spray or high-speed air with cold not less than 0.5 DEG C/s
But hot rolled plate is cooled to 150 DEG C~320 DEG C by speed；
The 3.3 secondary rolling process include: rolled plate, until reaching predetermined thickness, room temperature are then air-cooled to, wherein often
The deflection 5% to 20% of one rolling pass,；
The 3.4 solution hardening processing include: the plate solution hardening with room temperature water to 450 DEG C~550 DEG C；
It is 0.5~6.5% that the 3.5 pre-stretching processing, which include: that plate prestretching extends to deflection within 4h,；
The 3.6 artificial aging processing include: 110 DEG C~175 DEG C of single-stage artificial aging temperature or level-one aging temp 90
DEG C~two-stage time effects of 125 DEG C and 140~170 DEG C of secondary aging temperature.
A kind of preferred preparation method of aluminum alloy plate materials, thes improvement is that:
The temperature of the hot rolling treatment is 510 DEG C；
It is 250 DEG C that the rapid cooling processing, which stops cooling temperature,；
The temperature of the solution hardening processing is 500 DEG C；
The artificial aging processing, single-stage aging temperature are 135 DEG C；Two-stage time effect: 110 DEG C of level-one aging temp, second level
160 DEG C of aging temp.
Further a kind of preparation method of aluminum alloy plate materials, it is improved in that being rolled in the step 3.1 predetermined
Deflection stops when being 80%.
Further a kind of preparation method of aluminum alloy plate materials, it is improved in that being quickly cooled down in the step 3.2
Cooling velocity be 0.5 DEG C/s.
Further a kind of preparation method of aluminum alloy plate materials, it is improved in that secondary rolling in the step 3.3
When each rolling pass deflection be 15%.
Further a kind of preparation method of aluminum alloy plate materials, it is improved in that in the step 3.5 at pre-stretching
The stretcher strain amount of reason is 5%.
Compared with the immediate prior art, technical solution provided by the invention has following excellent effect:
1, technical solution provided by the invention can significantly improve alloy especially high alloy content aluminum alloy plate materials
Comprehensive performance while reducing alloy strength not, has the performances such as excellent fatigue, fracture, corrosion-resistant；
2, technical solution provided by the invention includes the journey in rapid cooling, temperature-controlled rolling and aluminum alloy plate materials preparation process
Sequence, method simple possible, industrialization exploitativeness are strong；
3, technical solution provided by the invention is by way of rapid cooling+temperature-controlled rolling, make large scale " Wei Shi body " with
And remaining second phase is resolved in the problem of crystal boundary " heredity ", is expanded the window of al alloy component design and preparation, is made
The preparation of industrialization of high alloy content aluminum alloy plate materials becomes feasible.
Detailed description of the invention
Fig. 1 is the 80mm plate longitudinal section mirco structure pattern by hot rolling
Fig. 2 is by hot rolling, and lotion is cooling, the 80mm plate longitudinal section mirco structure pattern of secondary hot rolling
Fig. 3 is by hot rolling, solution hardening+pre-stretching+ageing treatment 80mm plate longitudinal section mirco structure pattern
Fig. 4 is by hot rolling, and lotion is cooling, secondary hot rolling, and solution hardening+pre-stretching+ageing treatment 80mm plate is vertical
Section mirco structure pattern
Specific embodiment
The present invention is further illustrated combined with specific embodiments below, but the invention is not limited to following implementations
Example.
Embodiment one
Using method provided by the invention by the aluminium alloy flat bloom with a thickness of 400mm by weight percentage: Cu
3.5%, Li 1.7%, Mg 0.38%, Zn 8.0%, Mn 0.44%, Ag 0.35%, Zr 0.10%, Ti0.06%, Si
0.06%, Fe 0.08%, surplus Al are heated at a temperature of 510 ± 15 DEG C, after come out of the stove hot rolling, lotion is fast when being rolled down to 95mm
Speed is cooled to 250~300 DEG C, wherein being rolled down to 80mm with the deflection that draught per pass is 8%.The plate of rolling is dissolved
It quenches at (500 DEG C~540 DEG C/8h, room temperature water quenching)+pre-stretching processing (pre-tension deformation amount 3%~7%)+artificial aging
Reason (135 DEG C of aging process~165 DEG C/10~20h) is sampled from the plate after hot rolled plate and fixation rates respectively,
Mirco structure is observed, and is compared with the plate normally rolled, as a result as shown in Figure 1, Figure 2, Figure 3, Figure 4.Then, when measurement
The stretching of plate different directions, fracture toughness (K after effect processingIC) and intergranular, peeling, anti-stress corrosion performance (C ring) and
Fatigue crack growth rate (da/dN), the results are shown in Table 1.
Wherein remarks in table:
1. the Characterization of Tensile strength of materials, the index of plasticity, according to 228 canonical measure of GB/T, wherein L is to sample generation
Table is sampled along rolling direction (length direction)；LT is sampled to representative perpendicular to rolling direction (width direction)；ST is to representative along thickness
Spend direction sampling；
2. fracture toughness characterizes the index of material Resisting fractre ability, according to 4161 canonical measure of GB/T, wherein KICFor crackle
Stress state near tip is in plane strain state, and when Crack Tip Deformation suffers restraints, and material expands crackle
The drag of exhibition, unit MPa*m1/2；T-L represent the loading direction of fracture toughness sample as perpendicular to T to (i.e. strip width side
To) load, direction of crack propagation is extended along L to (i.e. panel length direction)；
3. fatigue crack growth rate characterizes the index of the antifatigue damage performance of material, according to 6398 canonical measure of GB/T,
Wherein AK is strength stress factor range；T-L represent the loading direction in fatigue crack growth rate sample as perpendicular to T to
(i.e. strip width direction) load, direction of crack propagation are extended along L to (i.e. panel length direction)；
4. anti-stress corrosion performance characterizes corrosion resistance of the material under external tensile stress and corrosive environment, according to
15970.5 canonical measure of GB/T, the direction S-L represent loading direction as perpendicular to S to (i.e. plate thickness direction) load, stress
Corrosion cracking propagation direction is extended along L to (i.e. panel length direction)；
5. Peeling Corrosion is the index for characterizing interlayer spalling resistance under material corrosion environment, surveyed according to 22639 standard of GB/T
Amount, FA represents the apparent aliquation in surface, and penetrates metal；EB is surface severe delamination, penetrates into metal depths.
It can be found that large scale " Wei will not be precipitated in the hot rolling in slab after handling by means of the present invention
Family name's body " tissue, fixation rates back wall are recrystallized around coarse second phase, become coarse second phase of distribution along crystal boundary
Transgranular distribution；Meanwhile the residual of large-size flaky " Wei Shi body " is not observed yet in crystal boundary, sub boundary position, to make slab
Under the premise of intensity does not reduce, plasticity, fracture toughness, corrosion resistance and fatigue crack growth rate are obtained and are significantly mentioned
Height, comprehensive performance are obviously improved.
Aluminium alloy capability comparison sheet of the table 1 through the present invention and conventional process
Embodiment two
Using method provided by the invention by the aluminium alloy flat bloom with a thickness of 300mm by weight percentage: Zn
11.2%, Mg 2.3%, Cu 1.5%, Mn 0.2%, Sc 0.06%, Zr 0.08%, Ti 0.03%, Si0.06%, Fe
0.10%, surplus Al, lotion is quickly cooled to 200~300 when hot rolling of coming out of the stove after heating at 420 ± 10 DEG C is to 62mm
DEG C, wherein being rolled down to 50mm with the deflection that draught per pass is 6~10%.By the plate solution hardening (472 ± 5 of rolling
DEG C/3h, room temperature water quenching)+pre-stretching processing (pre-tension deformation amount 0.5~1.5%)+artificial aging processing (aging process 120
± 5 DEG C/6~20h+145~165 DEG C/6~12h).Then, stretching, the fracture toughness, fatigue of the plate after ageing treatment are measured
Crack growth rate, peeling and anti-stress corrosion performance (C ring), the results are shown in Table 2.
With traditional method ratio, after the method for the present invention is handled, under the premise of slab intensity does not reduce, plasticity is broken
It splits toughness, fatigue crack growth rate, corrosion resistance to be significantly improved, comprehensive performance is obviously improved.
The performance comparison sheet of the aluminium alloy of the method for the invention of table 2 and conventional process
It is found by Tables 1 and 2: not being reduced after the method for the present invention is handled in slab intensity with traditional method ratio
Under the premise of, plasticity, fracture toughness, fatigue crack growth rate, corrosion resistance are significantly improved, and comprehensive performance is significant
It is promoted.
Claims (8)
1. a kind of preparation method of aluminum alloy plate materials, which is characterized in that alloy hot rolling, rapid cooling, secondary rolling, solid solution are quenched
Fire, pre-stretching and artificial aging processing；
By weight percentage, which contains: Zn 8.0~12.0%, Cu 1.0~6.5%, Li 1.4~1.80%, Mg
0.2~3.5%, Mn 0.10~1.30% and Zr 0.02~0.25%, Sc 0.05~0.35%, Ag 0.2~0.8%,
Any 1~4 kind in Er 0.10~0.25%, Si≤0.15%, Fe≤0.15%, Ti≤0.10%, other impurity are single≤
0.05%, total amount≤0.15%, surplus Al.
2. a kind of preparation method of aluminum alloy plate materials as described in claim 1, which is characterized in that the alloying component are as follows: Zn
8.0%, Cu 3.5%, Li 1.70%, Mg 0.38%, Mn 0.44% and Zr 0.10%, Sc 0.10%, Ag
Any 1~4 kind in 0.35%, Er 0.10, Si 0.06%, Fe 0.08%, Ti 0.06%, other impurity are single≤
0.05%, total amount≤0.15%, surplus Al.
3. a kind of preparation method of aluminum alloy plate materials as described in claim 1, it is characterised in that:
3.1 hot rolling treatments include: the blank material that stove heating is heated in hot rolling at 380 DEG C~560 DEG C, until predetermined deformation amount
75%~90%；
The 3.2 rapid cooling processing include: to be blown with lotion, spray or high-speed air with the cooling speed not less than 0.5 DEG C/s
Hot rolled plate is cooled to 150 DEG C~320 DEG C by degree；
The 3.3 secondary rolling process include: rolled plate, until reaching predetermined thickness, room temperature are then air-cooled to, wherein each roll
The deflection 5% to 20% of passage processed,；
The 3.4 solution hardening processing include: the plate solution hardening with room temperature water to 450 DEG C~550 DEG C；
It is 0.5~6.5% that the 3.5 pre-stretching processing, which include: that plate prestretching extends to deflection within 4h,；
3.6 artificial agings processing include: 90 DEG C of 110 DEG C~175 DEG C of single-stage artificial aging temperature or level-one aging temp~
125 DEG C and 140~170 DEG C of secondary aging temperature of two-stage time effect.
4. a kind of preparation method of aluminum alloy plate materials as described in claim 1, it is characterised in that:
The temperature of the hot rolling treatment is 510 DEG C；
It is 250 DEG C that the rapid cooling processing, which stops cooling temperature,；
The temperature of the solution hardening processing is 500 DEG C；
The artificial aging processing, single-stage aging temperature are 135 DEG C；Two-stage time effect: 110 DEG C of level-one aging temp, secondary time effect
160 DEG C of temperature.
5. a kind of preparation method of aluminum alloy plate materials as claimed in claim 3, which is characterized in that rolled in the step 3.1
Predetermined deformation amount stops when being 80%.
6. a kind of preparation method of aluminum alloy plate materials as claimed in claim 3, which is characterized in that in the step 3.2 quickly
Cooling cooling velocity is 0.5 DEG C/s.
7. a kind of preparation method of aluminum alloy plate materials as claimed in claim 3, which is characterized in that secondary in the step 3.3
The deflection of each rolling pass is 15% when rolling.
8. a kind of preparation method of aluminum alloy plate materials as claimed in claim 3, which is characterized in that prestretching in the step 3.5
The stretcher strain amount for stretching processing is 5%.
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Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
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| CN110331319A (en) * | 2019-05-27 | 2019-10-15 | 中国航发北京航空材料研究院 | It is a kind of containing scandium and the high-strength of erbium, high-ductility Alcoa and preparation method thereof |
| CN110423966A (en) * | 2019-07-29 | 2019-11-08 | 中国航发北京航空材料研究院 | A kind of preparation process improving aluminium lithium alloy product comprehensive performance |
| CN113718096A (en) * | 2021-09-08 | 2021-11-30 | 中国航发北京航空材料研究院 | Preparation process of aluminum-lithium alloy plate with high comprehensive performance |
| CN113774296A (en) * | 2021-09-08 | 2021-12-10 | 中国航发北京航空材料研究院 | Preparation process for improving comprehensive performance of aluminum alloy thick plate and forging |
| CN115874124A (en) * | 2022-12-07 | 2023-03-31 | 东北轻合金有限责任公司 | Thermomechanical treatment method for improving damage tolerance performance of 2xxx plate |
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Cited By (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN110331319A (en) * | 2019-05-27 | 2019-10-15 | 中国航发北京航空材料研究院 | It is a kind of containing scandium and the high-strength of erbium, high-ductility Alcoa and preparation method thereof |
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| CN113718096A (en) * | 2021-09-08 | 2021-11-30 | 中国航发北京航空材料研究院 | Preparation process of aluminum-lithium alloy plate with high comprehensive performance |
| CN113774296A (en) * | 2021-09-08 | 2021-12-10 | 中国航发北京航空材料研究院 | Preparation process for improving comprehensive performance of aluminum alloy thick plate and forging |
| CN113718096B (en) * | 2021-09-08 | 2023-11-21 | 中国航发北京航空材料研究院 | Preparation process of high-comprehensive-performance aluminum-lithium alloy plate |
| CN115874124A (en) * | 2022-12-07 | 2023-03-31 | 东北轻合金有限责任公司 | Thermomechanical treatment method for improving damage tolerance performance of 2xxx plate |
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